JPS62234690A - Wire for submerged arc welding of low temperature steel - Google Patents
Wire for submerged arc welding of low temperature steelInfo
- Publication number
- JPS62234690A JPS62234690A JP7674986A JP7674986A JPS62234690A JP S62234690 A JPS62234690 A JP S62234690A JP 7674986 A JP7674986 A JP 7674986A JP 7674986 A JP7674986 A JP 7674986A JP S62234690 A JPS62234690 A JP S62234690A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- strength
- weld metal
- toughness
- welding
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000003466 welding Methods 0.000 title claims abstract description 26
- 229910000831 Steel Inorganic materials 0.000 title claims description 11
- 239000010959 steel Substances 0.000 title claims description 11
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 239000002184 metal Substances 0.000 abstract description 40
- 229910052751 metal Inorganic materials 0.000 abstract description 40
- 238000005336 cracking Methods 0.000 abstract description 14
- 230000004907 flux Effects 0.000 abstract description 8
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 4
- 239000003795 chemical substances by application Substances 0.000 abstract description 4
- 229910052710 silicon Inorganic materials 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 229910052681 coesite Inorganic materials 0.000 abstract description 2
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 2
- 229910052735 hafnium Inorganic materials 0.000 abstract description 2
- 229910052761 rare earth metal Inorganic materials 0.000 abstract description 2
- 239000000377 silicon dioxide Substances 0.000 abstract description 2
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 2
- 229910052682 stishovite Inorganic materials 0.000 abstract description 2
- 229910052905 tridymite Inorganic materials 0.000 abstract description 2
- 229910052727 yttrium Inorganic materials 0.000 abstract description 2
- 229910052782 aluminium Inorganic materials 0.000 abstract 2
- 229910052749 magnesium Inorganic materials 0.000 abstract 1
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 229910052719 titanium Inorganic materials 0.000 abstract 1
- 229910052726 zirconium Inorganic materials 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 11
- 239000000956 alloy Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 239000000463 material Substances 0.000 description 10
- 239000010949 copper Substances 0.000 description 9
- 230000007423 decrease Effects 0.000 description 6
- 229910003296 Ni-Mo Inorganic materials 0.000 description 5
- DDTIGTPWGISMKL-UHFFFAOYSA-N molybdenum nickel Chemical compound [Ni].[Mo] DDTIGTPWGISMKL-UHFFFAOYSA-N 0.000 description 5
- 229910052760 oxygen Inorganic materials 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 239000010953 base metal Substances 0.000 description 4
- 239000012895 dilution Substances 0.000 description 4
- 238000010790 dilution Methods 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 3
- 230000009931 harmful effect Effects 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 229910000856 hastalloy Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 235000019353 potassium silicate Nutrition 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 2
- 238000003860 storage Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 239000008186 active pharmaceutical agent Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、ＬＮＧ等の貯槽タンクとして、極低温で使用
される９％Ｎｉ鋼等の低温用鋼のサブマージアーク溶接
ワイヤに係り、特に溶接金属の強度を高め、溶接部の安
全性を確保しつつ、経済的な溶接を可能にするワイヤ成
分に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to a submerged arc welding wire for low-temperature steel such as 9% Ni steel used at extremely low temperatures as a storage tank for LNG, etc., and particularly for welding. It relates to wire components that enable economical welding while increasing the strength of metals and ensuring the safety of welded parts.
（従来の技術）
近年、石油代替エネルギーとしてＬＮＧが注目を集め、
各地にタンクが建造されている。ＬＮＧの貯蔵用円筒タ
ンクは、主に９％Ｎｉ鋼を用い、溶接によって製作され
るが、その極低温における使用環境から、浴接部に対し
て優れた低温靭性、強度あるいは耐割れ性等か要求され
ている。(Conventional technology) In recent years, LNG has attracted attention as an energy alternative to oil.
Tanks are being built all over the place. Cylindrical tanks for LNG storage are mainly made of 9% Ni steel and manufactured by welding, but due to the extremely low temperature environment in which they are used, they have excellent low-temperature toughness, strength, and crack resistance for bath contact parts. requested.
従って、浴接材料としても、これらの厳しい要求性能を
満足するたの、浴接用心線としてＮｉ基合金か用いられ
、破性アーク浴接、サブマージアーク溶接、ガスシール
ドアーク液液に適用されている。Therefore, in order to satisfy these strict performance requirements, Ni-based alloys are used as bath welding materials and are applied to rupture arc bath welding, submerged arc welding, and gas-shielded arc liquid. There is.
又、Ｎｉ基合金の中でも、Ｎｉ−Ｍｏを主成分とするハ
ステロイ合金が、普温割れ感受性か良好であり、これを
利用してサブマージアーク温液用ワイヤが開発されてい
る。例えば、特公昭４．９−２７７３２号公報や、特公
昭５１−２９１０４号公報記載のＮ１基合金が実用化さ
れている。また、Ｎ１、Ｉｖｉｏ、Ａｔを含有している
ものとして、特開昭５８−６１９９３号公報や、特公昭
５９−６７５６号公報、特開昭６０−２４７４９３号公
報に提案されている。Furthermore, among Ni-based alloys, Hastelloy alloy containing Ni-Mo as a main component has good susceptibility to cold cracking, and submerged arc hot liquid wires have been developed using this. For example, N1-based alloys described in Japanese Patent Publication No. 4.9-27732 and Japanese Patent Publication No. 51-29104 have been put into practical use. In addition, materials containing N1, Ivio, and At have been proposed in JP-A-58-61993, JP-A-59-6756, and JP-A-60-247493.
しかしながら、従来から提案されたＮｉ −Ｍｏ基合金
は、それによって生成される溶接金属そのものは、母材
と同程度の引張強さを示すか、実継手に用いると母材希
釈により、溶接金属の引張強さは、母材に比べて低下す
る傾向がある。この傾向は溶接電流が高く、母材希釈率
の大きいサブマージアーク溶接において大きく、この強
度の低下は、タンク設計上重大な影響を及ぼし、これを
補償するため、板厚の厚いタンクを設計することが必要
となる。However, the weld metal produced by the Ni-Mo based alloys that have been proposed so far either exhibits tensile strength comparable to that of the base metal, or when used in actual joints, the weld metal is diluted due to base metal dilution. Tensile strength tends to be lower than that of the base material. This tendency is large in submerged arc welding where the welding current is high and the base metal dilution ratio is large. This decrease in strength has a serious effect on tank design, and to compensate for this, tanks with thick plates must be designed. Is required.
例えば平板円筒形タンクの側板算定式は次式囚で求めら
れる。For example, the equation for calculating the side plate of a flat cylindrical tank is given by the following formula.
ｔ ＝ ＰＤ／２ ｆ ・・・・・・ 囚ここで ｔ
：側板の板厚、Ｐ：液頭圧、Ｄ：直径、ｆ：材料強度を
示す。t = PD/2 f ...... Prisoner here t
: Thickness of side plate, P: Liquid head pressure, D: Diameter, f: Material strength.
即ち材料強度ｆが大であれば、それだけ板厚ｔを小さく
することが出来るのであるが、前述のごとく、溶接金属
の強度は、母材のそれに達しておらず、材料強度ｆは、
強度の低い溶接金属をベースにする必要かある。In other words, the greater the material strength f, the smaller the plate thickness t can be.However, as mentioned above, the strength of the weld metal does not reach that of the base metal, and the material strength f is
Is it necessary to use low-strength weld metal as the base?
ところで、９％Ｎｉ鋼の引張強さは７ Ｑ Ｋ４ ／ｒ
ｒｒｍ２以上、降伏強度は６０に９ｆ／叩ｎ２以上であ
るが、ＡＰＩか規定するＬＮＧタンクの設計における最
大許容応力値は、溶接金属の強度として、引張強さを１
００．０００ ＰＳｉ （７０，３に９ｆ／＋ｎｍ２）
、降伏強さ５５．０００ＰＳ ｉ （４０，８に９ｆ／
咽２）を基準とすることが可能であるように規定され、
母材と同等の引張強さでの設計が許されるようになり、
溶接金属の筒強度化が重要な課題となってきた。By the way, the tensile strength of 9% Ni steel is 7 Q K4 /r
rrm2 or more, the yield strength is 60 to 9f/n2 or more, but the maximum allowable stress value in the design of LNG tanks specified by API is the tensile strength 1 as the strength of the weld metal.
00.000 PSi (70,3 to 9f/+nm2)
, yield strength 55.000PS i (40,8 to 9f/
It is stipulated that it is possible to use the throat 2) as a standard,
It is now possible to design with tensile strength equivalent to that of the base material,
Increasing the strength of weld metal tubes has become an important issue.
ところが、前述の１’Ｊｉ −Ｍｏ基心線において、高
強度の溶接金属を得ようとすると、低温靭性が極端に低
下したり、高温割れ感受性が劣化する問題があり、溶接
金属の高強度化は、未だ達成はされていないのが現状で
ある。However, when trying to obtain a high-strength weld metal with the 1'Ji-Mo base line mentioned above, there are problems such as an extreme decrease in low-temperature toughness and deterioration of hot cracking susceptibility. The current situation is that this has not yet been achieved.
（発明が解決しようとする問題点）
本発明は、低温用Ｎｉ合金銅の高強度を有効に活用し、
安全の高いタンク設計に寄与すると共に、板厚の減少を
はかり、経済的なタンクを建造すべく、高強度溶接金属
として、引張強さ７１． Ｋｇｆ／ｒｒｒｍ２以上、降
伏強さ４ ］、 Ｋ９ｆ ／Ｔｍｎ２以上を確保し、そ
の上で、侵れた低温靭性と耐高温割れ感受性を有する溶
接金属を、生成し得る新規なサブマージアーク溶接用ワ
イヤを提供することを目的とするものである。(Problems to be solved by the invention) The present invention effectively utilizes the high strength of Ni alloy copper for low temperature use,
In order to contribute to a highly safe tank design, reduce the plate thickness, and build an economical tank, we used a high-strength weld metal with a tensile strength of 71. Kgf/rrrm2 or more, yield strength 4], K9f/Tmn2 or more, and on top of that, a new submerged arc welding wire that can produce a weld metal with excellent low-temperature toughness and high-temperature cracking resistance. The purpose is to provide
（問題点を解決するための手段）
本発明の要旨は、Ｃｒ ３．５％」ジ、下、（重量係以
下同様）、Ｎｉ６０〜８０％、Ｍｏ １．５〜２５％、
Ｗ４．０〜７．５％、Ｃｕ２．０％以下、Ａ７．０．１
６〜２．０％を含有し、かつ、Ｓｉ０．１４％以下に限
定したことを特徴とするサブマージアーク溶接用ワイヤ
にある。(Means for Solving the Problems) The gist of the present invention is as follows: Cr 3.5% (same as below), Ni 60-80%, Mo 1.5-25%,
W4.0-7.5%, Cu2.0% or less, A7.0.1
A wire for submerged arc welding is characterized in that it contains 6 to 2.0% Si and is limited to 0.14% or less.
（作用）
本発明ワイヤは、Ｎｉ −Ｍｏ基合金をベースとするも
のであるが、単にＮｉ−Ｍｏ基合金を、ザブマージアー
ク溶接用ワイヤに用いると、前述の如く、母材希釈によ
り合金のレベルが全体的に下がり、強度が低下する傾向
があり、この対策として母材希釈を考属して、多めの合
金を添加したワイヤの開発が強く望まれている。(Function) The wire of the present invention is based on a Ni-Mo based alloy. However, if a Ni-Mo based alloy is simply used as a submerged arc welding wire, as described above, the alloy will be diluted due to base material dilution. There is a tendency for the overall level to decrease and the strength to decrease, and as a countermeasure to this problem, there is a strong desire to develop a wire in which a larger amount of alloy is added by considering dilution of the base material.
即ち、溶接金属の強度を向上する手段としては、まず、
（１） Ｃｒ 、 Ｍｏ 、 Ｗ 、 Ｃｕなどの固溶
強化元素を添加又は増加する。（２）Ｃを添加し、炭化
物を析出させ、析出硬化をはかる。の２点が有効である
。That is, as a means to improve the strength of weld metal, first of all,
(1) Adding or increasing solid solution strengthening elements such as Cr, Mo, W, and Cu. (2) Add C to precipitate carbides to achieve precipitation hardening. Two points are valid.
しかしながら、このような元素は、強度を向上させる効
果を有しながら、適正量以上に添加すると、低温靭性お
よび耐割れ性を劣下せしめる有害性を有しており、単純
にこれら元素による強度向上をはかることは出来ない。However, while these elements have the effect of improving strength, if they are added in more than an appropriate amount, they have the harmful effect of deteriorating low-temperature toughness and cracking resistance. cannot be measured.
このような有害性の最も著しいものは、Ｃ，Ｃｒであり
、これらは靭性、耐割れ性の両者を著しく劣化させる。The most harmful substances are C and Cr, which significantly deteriorate both toughness and cracking resistance.
又、Ｍｏ 、Ｗ、Ｃｕは、耐割れ性については特に有害
性はみられないが、多量添加により、低温靭性を劣化さ
せることは避けることが出来ない。Furthermore, although Mo, W, and Cu do not appear to be particularly harmful to cracking resistance, their addition in large amounts inevitably deteriorates low-temperature toughness.
従って、高強度溶接金属の設計は、これらの点に対する
十分な対策を施した上で行なうことが必要であり、耐割
れ性、低温靭性の十分優れた溶接材料にしておくことが
必要である。Therefore, when designing a high-strength weld metal, it is necessary to take sufficient measures to address these points, and it is necessary to use a welding material that has sufficiently excellent cracking resistance and low-temperature toughness.
即ち、本発明においては、このような観点から、高強度
設計のベースとなる溶接金属成分について検討した結果
、Ｎｉ：６０〜８０％、Ｍｏ ： １５〜２５％を含有
するハステロイ系ワイヤにおいて、Ｃｒ：３．５％以下
、Ａｔ：０．１６〜２０％を含有させ、かつ、Ｓｉ ：
０．１４％以下に限定してお（ことか極めて重要であ
り、その上で、強度向上対策として、Ｗ：４０〜７５％
、Ｃｕ ： ２．０％以下を添加することが必要である
ことが判明した。That is, in the present invention, from this viewpoint, as a result of studying the weld metal components that are the basis of high-strength design, in a Hastelloy wire containing Ni: 60 to 80% and Mo: 15 to 25%, Cr : 3.5% or less, At: 0.16 to 20%, and Si:
W: 40 to 75% as a strength improvement measure.
, Cu: It was found that it was necessary to add 2.0% or less.
本発明ワイヤにおいては、Ｎ１６０〜８０％を金回する
が、Ｎｉは溶接金属組織をオーステナイト化し、−１，
９６℃という極低温における靭性を確保するために必須
の成分である。In the wire of the present invention, 160 to 80% of N is gold-plated, but Ni changes the weld metal structure to austenite, -1,
It is an essential component to ensure toughness at extremely low temperatures of 96°C.
このためには、ワイヤには６０％以上のＮｉを添加づ−
ることか必要である。しかし、溶接金属の強度を確保す
るためには、Ｍｏ 、 Ｗ等の他の元素も必要であり、
これを考慮すると、Ｎｉは８０％が上限である。従って
本発明ワイヤにおけるＮ１含有量は６０〜８０％である
。For this purpose, 60% or more Ni should be added to the wire.
It is necessary. However, in order to ensure the strength of weld metal, other elements such as Mo and W are also required.
Considering this, the upper limit for Ni is 80%. Therefore, the N1 content in the wire of the present invention is 60-80%.
なお、９％Ｎｉ鋼等の低温用鋼の溶接継手部は、極低温
環境にさらされるため、規格としては一１９６℃での低
温靭性が要求される。Note that welded joints of low-temperature steel such as 9% Ni steel are exposed to cryogenic environments, and therefore low-temperature toughness at -196° C. is required as a standard.
Ｍｏは、耐割れ性を低下させないで、溶接金属の強度を
高めるために極めて効果があるが、１５％未満では本効
果は認められない。しがしながら２５％を超えると、溶
接金属の低温靭性が低下し、好ましくない。従って、Ｍ
ｏ含有量は、１５〜２５％とする。Mo is extremely effective in increasing the strength of weld metal without reducing cracking resistance, but this effect is not observed when it is less than 15%. However, if it exceeds 25%, the low-temperature toughness of the weld metal decreases, which is not preferable. Therefore, M
o content is 15 to 25%.
次に本発明ワイヤにおいては、Ａ／＝ ０．１６〜２０
％、ＳｉＯ，１４％以下に限定するが、Ｓｌは耐割れ性
と靭性の両者を劣化せしめるものであり、高強度溶接金
属・を生成するワイヤとしては、Ｓｉを充分低減してお
くことが必要である。Next, in the wire of the present invention, A/=0.16 to 20
%, SiO, is limited to 14% or less, but since Sl deteriorates both cracking resistance and toughness, it is necessary to reduce Si sufficiently for wires that produce high-strength weld metal. It is.
しかしながら、Ｓｉは脱酸剤としては極めて重要な成分
であり、単にＳｌを低減することは、逆に溶接金属の酸
素が増太し、靭性劣化を招くこととなる。そこで、溶接
金属の酸素を増力目させないで、Ｓｉの低減を達成する
ためＳｉ以外の脱酸剤について、裡々検討した結果、Ａ
Ａが耐割れ性を損なわないで、溶接金属の酸素の低減に
著しい効果があることか判明した。However, Si is an extremely important component as a deoxidizing agent, and simply reducing Si will conversely increase oxygen in the weld metal, leading to deterioration of toughness. Therefore, as a result of careful consideration of deoxidizing agents other than Si in order to reduce Si without increasing the oxygen in the weld metal, we found that A
It was found that A had a remarkable effect on reducing oxygen in the weld metal without impairing cracking resistance.
酸素の低減は、低温靭性の向上に極めて有効であり、
Ｗ、 Ｍｏの添加により靭性劣化があっても、規格値（
Ｖ Ｅ １９６ ’：２３．５ Ｋｇｆ −ｍ ）を満
足する優れた靭性が得られるようになった。Reducing oxygen is extremely effective in improving low temperature toughness.
Even if the toughness deteriorates due to the addition of W and Mo, the standard value (
Excellent toughness satisfying V E 196': 23.5 Kgf -m can now be obtained.
以上のようなＡｔの効果を得るには、ワイヤ中のＳｉを
０．１４％以下に限定し、かつ、Ａｔを０．１６％以上
添加することか必要である。しかしながら１、Ｍを２．
０％を超えて添加すると、ワイヤの製造時における鍛造
性が劣化し、ワイヤとして健全なものが出来な（なるの
で、ＡＡは２％以下にすることが必要である。In order to obtain the above effects of At, it is necessary to limit Si in the wire to 0.14% or less and to add At at 0.16% or more. However, 1, M is 2.
If it is added in excess of 0%, the forgeability during wire manufacturing will deteriorate, making it impossible to produce a sound wire. Therefore, it is necessary to keep AA at 2% or less.
次にＣｒ ３．５％以下を含有する理由であるが、Ｃｒ
は前述の如く、溶接金属の強度を向上させる効果がある
。さらに、ワイヤ製造時における鍛造性を改善する効果
があるので、一定量を添加することが好ましい。Next, the reason for containing 3.5% or less of Cr is that
As mentioned above, this has the effect of improving the strength of the weld metal. Furthermore, since it has the effect of improving forgeability during wire manufacturing, it is preferable to add a certain amount.
特に本発明ワイヤの如＜ Ｎｉ −Ｍｏ基合金の如く、
多量のＡｔあるいはＷが添加されていると、鍛造夛留率
か著しく減少する。しかしながら、少量のＣｒの添加と
ともに歩留り率は上昇し、歩留り率を改善することが出
来る。但し、Ｃｒ含有量が３５％を超えると、溶接金属
の高温での延性が急激に低下し、割れ発生の原因となる
。従って、Ｃｒ含有量は、３．５％以下とする。In particular, as in the wire of the present invention, as in the case of a Ni-Mo based alloy,
When a large amount of At or W is added, the forging retention rate is significantly reduced. However, the yield rate increases with the addition of a small amount of Cr, making it possible to improve the yield rate. However, if the Cr content exceeds 35%, the ductility of the weld metal at high temperatures decreases rapidly, causing cracking. Therefore, the Cr content is set to 3.5% or less.
次に本発明のワイヤにおいては、Ｗを４０〜７５％とす
るか、Ｗは溶接金属の高強度化に最も有効であり、本発
明のために必須の成分である。Next, in the wire of the present invention, W is set to 40 to 75%, or W is most effective in increasing the strength of the weld metal and is an essential component for the present invention.
第１図は、浴接金属の引張特性に及ぼすワイヤ中のＷ含
有量の影響を示すものであり、Ｗが４％以上において、
安定して降伏強さく０２％耐力）４１にりｆ／（転）２
以上、引張強さ７１に９ｆ／膿２以上の強度を得ること
が可能となる。Figure 1 shows the influence of the W content in the wire on the tensile properties of the bath-welded metal.
Stable yield strength (02% yield strength) 41 f/(transition) 2
As described above, it is possible to obtain tensile strength 71 of 9f/pus2 or more.
なお、本溶接に用いたフラックスおよび鋼板は、実施例
（第２、第３表）に示すものと同様であり、又溶接条件
は、第４表のＷＣ−１に示したものと同様である。The flux and steel plate used for this welding were the same as those shown in Examples (Tables 2 and 3), and the welding conditions were the same as those shown in WC-1 in Table 4. .
ところで、前述の如く溶接金属の強度向上に伴い、靭性
の劣化現象が認められ、これを考慮して、Ｗの量を選ぶ
ことか必要である。しかしながら、本発明においては、
ワイヤ中のＳｉを低減し、Ａｔを添加することにより、
ベースとなる溶接金属靭性を著しく向上することが出来
た。By the way, as mentioned above, as the strength of the weld metal increases, a phenomenon of deterioration of toughness is observed, and it is necessary to take this into consideration when selecting the amount of W. However, in the present invention,
By reducing Si in the wire and adding At,
We were able to significantly improve the base weld metal toughness.
第２図に、Ａｔ含有量の異なるワイヤにおいて、靭性に
及ぼすワイヤ中のＷの影響について検討した結果を示す
。FIG. 2 shows the results of examining the influence of W in wires on toughness in wires with different At contents.
ワイヤ中にＡｚを０１６％以上添加することにより、Ｗ
を４〜７．５％含再させても、優れた靭性を示すことが
可能であることが判る。By adding 0.16% or more of Az into the wire, W
It can be seen that excellent toughness can be exhibited even when the content is 4 to 7.5%.
即ち、本発明ワイヤにおいては、強度向上のため、Ｗを
４％以上添加するが、７．５％を超えると、たとえＡｔ
を添加したワイヤでも、靭性が劣化するので、−Ｗの添
加量は７５％以下にすることが必要である。That is, in the wire of the present invention, 4% or more of W is added to improve strength, but if it exceeds 7.5%, even At
Even in wires to which -W is added, the toughness deteriorates, so the amount of -W added needs to be 75% or less.
なお、第２図の検討に用いた鋼板およびフラックスおよ
び溶接条件は、第１図の場合と同じものである。Note that the steel plate, flux, and welding conditions used in the study of FIG. 2 are the same as in the case of FIG. 1.
次に本発明において、２．０％以下のＣｕを添加する理
由であるが、Ｃｕは溶接金属の靭性を損なわない範囲の
少量の添加で、強度向上に有効であることが判明した。Next, in the present invention, the reason for adding 2.0% or less of Cu is that it has been found that adding Cu in a small amount within a range that does not impair the toughness of the weld metal is effective in improving the strength.
前述のように、いたずらに溶接金属の強度をあげると、
靭性が劣化する傾向がある。As mentioned above, if you unnecessarily increase the strength of the weld metal,
Toughness tends to deteriorate.
そこで良好な靭性な保ちつつ、高強度化を達成するには
、Ｗの添加とともに、少量のＣｕの添加が非常に有効な
方法である。しかしながら、Ｃｕが２０％を超えると、
浴接金属の靭性が劣化するので、ワイヤ中のＣｕは２．
０％以下に限定することが必要である。Therefore, in order to achieve high strength while maintaining good toughness, adding a small amount of Cu in addition to W is a very effective method. However, when Cu exceeds 20%,
Since the toughness of the bath-welded metal deteriorates, Cu in the wire is 2.
It is necessary to limit it to 0% or less.
以上、本発明における必須成分および限定成分について
詳述したが、本発明においてはＰ、Ｓ等の不可避不純物
の他に、（１）強度向上を目的として、Ｃ，Ｃｏ、庵等
（２）脱酸剤として、ｒ１、ｌｌＶＩｇ、Ｃａ、■、Ｚ
ｒ 、 Ｙ 、 Ｈｆ 、 ＲＥＭ等（３）曲げ性能向
上のためのＢ等、又ある程度のＦｅも含有することか出
来る。The essential components and limited components in the present invention have been described in detail above, but in the present invention, in addition to unavoidable impurities such as P and S, (1) C, Co, and other substances are added for the purpose of improving strength. As an acid agent, r1, llVIg, Ca, ■, Z
r, Y, Hf, REM, etc. (3) B, etc. for improving bending performance, and a certain amount of Fe can also be contained.
なお、本発明は、サブマージアーク溶接ワイヤに関する
ものであるか、以上に述べた会金成分は、フラックスか
ら粉粒物としても添加することが出来るが、フラックス
からの添加は、溶接金属への移行量が、浴接条件に影響
を受けることが太きいため、不安定となり、常に目的の
溶接金属を得ることが困難であり、本発明においては、
必須成分についてはワイヤから添加することが必要であ
る。The present invention relates to a submerged arc welding wire, and the above-mentioned metal components can be added from flux as powder or granules; Since the amount is greatly affected by the bath welding conditions, it becomes unstable and it is difficult to always obtain the desired weld metal.
It is necessary to add essential components from the wire.
ところで、組み合わせるフラックスとしては、低Ｓｉ−
低酸素溶接金属を得るため、実質「９にＳｉを含有せず
、又、ＳｉＯ２を必要最小限にとどめ、かつ高塩基にす
ることを考慮して、ＣａＯ： ５〜２０％、ＣａＦ、、
： １０〜６０％、Ａｔ２０３：１０〜３０％、５１
０２：］００％以下■０４〜３０％、ＣＯＺ相当量：１
〜５％、Ａｔ： ５％以下、その他（水ガラス、固形分
等）を含有するものが望ましい。By the way, as the flux to be combined, low Si-
In order to obtain a low-oxygen weld metal, in consideration of substantially not containing Si, keeping SiO2 to the necessary minimum, and making it a high base, CaO: 5 to 20%, CaF,...
: 10-60%, At203: 10-30%, 51
02: ] 00% or less ■ 04-30%, COZ equivalent amount: 1
~5%, At: 5% or less, and those containing others (water glass, solid content, etc.) are desirable.
この場合のＡｔの添加は、溶接中のワイヤ中Ａｔの消耗
による不足を、防止することを目的としている。The purpose of adding At in this case is to prevent a shortage due to consumption of At in the wire during welding.
（実施例）
第１辰に示す組成の合金を真空溶解炉にて作製し、鍛造
、圧延、線引を行なって、３２酎ダ、２４ｍｕ ｉのワ
イヤを得た。第１表において、Ｗ−１〜Ｗ−７は本発明
例であり、Ｗ−８〜Ｗ−１８は比較例を示したものであ
る。但し、Ｗ−１３は熱間鍛造中に亀裂か多数発生し、
線引できなかった。組み合わせるフラックスとしては、
第２表に示す組成の焼成形フラックスを用いた。(Example) An alloy having the composition shown in the first section was produced in a vacuum melting furnace, and was forged, rolled, and wire-drawn to obtain a wire of 32 mm and 24 mm. In Table 1, W-1 to W-7 are examples of the present invention, and W-8 to W-18 are comparative examples. However, many cracks occurred in W-13 during hot forging,
I couldn't draw the line. The flux to be combined is
A sintered flux having the composition shown in Table 2 was used.
フラックスは、原料粉を水ガラスで混和し、約５００℃
で乾燥し、フシックス粒度の９０％が、１２Ｘ１．ＯＯ
メツシュになるよう製造した。Flux is made by mixing the raw material powder with water glass and heating it to about 500℃.
90% of the Fusix particle size was 12X1. OO
Manufactured to become mesh.
上記溶接用ワイヤについて、第３表に示す鋼板および第
４表および第３図に示′ｆ浴接条件により、１７種のサ
ブマージアーク溶接を実施した。溶接長は１．５ｍであ
る。Seventeen types of submerged arc welding were performed using the above welding wires using the steel plates shown in Table 3 and the bath welding conditions shown in Table 4 and FIG. 3. The weld length is 1.5 m.
第５表に実施した溶接におけるワイヤおよび溶接部の離
性試験結果を示す。Table 5 shows the results of the release test for wires and welds during welding.
溶接部の確性は、第４図に示すように、余盛りビードを
板面まで研削した後、Ｘ線透過試鯨を行ない、高温割れ
の有無を確認した。To check the accuracy of the weld, as shown in Figure 4, after grinding the excess bead to the plate surface, an X-ray transmission test was conducted to check for hot cracks.
第５表にはＸ線透過試植で観察された割れ長さの合計を
、１ｍ当りの長さで示した。さらに溶接金属より引張試
験片１） （ＪＩＳ Ｚ ３１１１． Ａ２号）および
衝撃試験片（１（ＪＩＳ Ｚ ２２０２４号）を採取し
、それぞれの試験を行なった。衝撃試験は、ＬＮＧタン
ク溶接部に要求される一１９６℃で行なった。Table 5 shows the total length of cracks observed in the X-ray transmission trial planting, expressed as length per 1 m. Furthermore, a tensile test piece 1) (JIS Z 3111.A2) and an impact test piece (1 (JIS Z 22024)) were taken from the weld metal and tested. The test was carried out at -196°C.
す、上の溶接部の確性結果を、第４表右欄に示す。The accuracy results for the upper weld are shown in the right column of Table 4.
実施例のうち、扁１〜煮７は、本発明例の効果により優
れた溶接部を得ることが出来たか、届８〜Ａ １７は第
５表にその個々の理由について示した如く、ワイヤ中の
Ｎｉ 、 Ｍｏ 、 Ｗ、Ｃｕ、 ＡＡ、 Ｃｒおよび
Ｓ１含有量の不適正により、割れの発生、強度不足、衝
撃１直不足の問題か発生した。Among Examples, in Examples 1 to 7, it was possible to obtain excellent welds due to the effects of the present invention, and in cases 8 to A 17, as shown in Table 5 for the individual reasons, it was found that excellent welds were obtained in the wire. Inappropriate Ni, Mo, W, Cu, AA, Cr, and S1 contents caused problems such as cracking, insufficient strength, and insufficient impact strength.
（発明の効果）
以上述べた如く、本発明は低温用Ｎｉ合金鋼の尚強度を
有効に活用すべく、高強度溶接金属として、引張強さ７
１に９ｆ／ｍｍ２以上、降伏強さ４． ］ Ｋｑｆ／ｗ
ｎ２以上を確保し、その上で優れた低温靭性と、高温割
れ感受性か良好な溶接金属を生成し得て、その工業的効
果は大である。(Effects of the Invention) As described above, the present invention provides a high-strength weld metal with a tensile strength of 7.
1 to 9f/mm2 or more, yield strength 4. ] Kqf/w
It is possible to secure n2 or more, and on top of that, produce a weld metal with excellent low temperature toughness and good hot cracking susceptibility, which has great industrial effects.
第１図は溶接金属の引張特性に及ぼすワイヤ中のＷ含有
量の影響を説明する線図、第２図は溶接代理人 弁理士
茶野木 立 夫
０２４６８１θ
ワイヤ中のＷ量（重量％）
ワイヤ中のＷ量（重量％）
（θ）
（ｂ）Figure 1 is a diagram explaining the influence of the W content in the wire on the tensile properties of weld metal, and Figure 2 is a diagram explaining the influence of the W content in the wire on the tensile properties of weld metal. W amount (weight%) (θ) (b)
Claims (1)
ク溶接用ワイヤ。[Claims] Contains in weight percent Cr 3.5% or less, Ni 60-80%, Mo 15-25%, W 4.0-7.5%, Cu 2.0% or less Al 0.16-2.0%, and Si0 A wire for submerged arc welding of low temperature steel, characterized in that the content is limited to 14% or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7674986A JPS62234690A (en) | 1986-04-04 | 1986-04-04 | Wire for submerged arc welding of low temperature steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7674986A JPS62234690A (en) | 1986-04-04 | 1986-04-04 | Wire for submerged arc welding of low temperature steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62234690A true JPS62234690A (en) | 1987-10-14 |
Family
ID=13614244
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7674986A Pending JPS62234690A (en) | 1986-04-04 | 1986-04-04 | Wire for submerged arc welding of low temperature steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62234690A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010274268A (en) * | 2009-05-26 | 2010-12-09 | Sumitomo Metal Ind Ltd | Welding material and welding joint |
| JP2011056562A (en) * | 2009-09-11 | 2011-03-24 | Nippon Steel & Sumikin Welding Co Ltd | Method for submerged arc welding of steel for low-temperature service |
-
1986
- 1986-04-04 JP JP7674986A patent/JPS62234690A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010274268A (en) * | 2009-05-26 | 2010-12-09 | Sumitomo Metal Ind Ltd | Welding material and welding joint |
| JP2011056562A (en) * | 2009-09-11 | 2011-03-24 | Nippon Steel & Sumikin Welding Co Ltd | Method for submerged arc welding of steel for low-temperature service |
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